Treatment of steel or iron



Feb. 427, 1945. H, T CHANDLE'R 2,370,289

TREATMENT OF STEEL OR IRON Filed July 18, 1940 3 Sheets-Sheet 1 4 zr .5.86 4 ,s 6.07

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w e 4. 0 4 k 13 /in 5 3x-Hr ,o n Q, 25 b? .I 8 on o 7 /o W Q 4.00 o 295 6 Al Iv 'AAA ga l v :AQ-t' v 7 v INVENTOR A 1 g* I* l 'Anuman-rmi 5,6; Henry?? f1 lnhandler.

H. T. CHANDLER 2,370,289

TREATMENT 0F STEEL OR IRON h Filed July 18, 1940 Feb. 27, 1945.

3 Sheets-Sheet 2 .03 6. 25 A A AVVA e AvAvAvAv 'i ver/Avn; VA

v? is Am.' o A 5.86 2 .Q9 go l O 7 \`/ENTOR .HenryT.

Patented Feb. 27, 1945 vUNITED STATES PATENT OFFICE TREATMENT F STEEL 0R IRON Henry r. chandler, New York, N. Y., wenn, by mesne assignments, to Vanadium Corporation of America, New York, N. Y., a corporation of Delaware Application July 1s, 1940, sei-n1 No. 346,111

17 Claims.

to fatigue and impact, or other useful engineering property of the steel which defines its suitability for some particular service, or an improvement in those less clearly defined characteristics such as forgeability, machinability, response to heat treatment, etc., which determine the ease of fabrication of the steel `from the ingot to the nished part. Largely because of this iniluence of alloy elements, steel has become a most versatile en gineering material. Alloy steels are now regu-A larly made to hundreds of different specications of widely diverse physical, chemical and electri- `cal properties and suit-ed to a. wide variety o'f structural uses.

For convenience, these auxiliary elementsvare usually added to the steel in the form of iron alloys, although in some cases, for example, nickel, copper and aluminum, the metals themselves are used. Thus there has appeared on the market a large group of metal products such as ferrosilicon, ferro-chromium. ferro-tungsten, silicomanganese, etc., etc., which are prepared specically for the purposes of the steel making industry and which are generally referred to as ferro-alloys.

Broadly speaking, the commercial value of these ferro-alloys is based upon two distinct, though related, functions which they perform in modern steel making practice. First, they serve as a convenient means of adding to the base composition of the steel a desired quantity of one or more of the useful steel alloying elements. The presence as a part of the composition of the finished steel, of specied quantities of these added elements has an important influence on the complex equilibrium of the iron-carbon system of the solid steel and because of this, as well as their alloying effect and other reasons, the properties of the finished steel are thereby altered in some desirable manner.y

An extensive art has been built up around this use of ferro-alloys and the steels in which they,

` are used are commonly known as "Alloy steels.

Such steels are generally classied and named in accordance with the predominating element or elements added. Thus, we have nickel steels, y n

chromium steels, lvanadium steels, chromiumvanadium steels, tungsten steels. The 'ferroalloys produced for making this class of steel may be conveniently called Addition alloys, inasmuch as the maior purpose is for the addition'of some alloying element to the composition of the ilnished steel.

In contrast to this truly alloying eil'ect, y dition of certain elements to a steel bath may also profoundly inuence the physical properties of i the finished steel in quite another manner.

It is quite commonly known that wide variations in steel quality may result from variations in furnace operation for a steel of a given chemical composition. The molten steel bath, from the time the charge is melted until it is poured and solidied, is the scene of a highly complicated set of physical and chemical reactions between the various elements and their compounds which l make up the composition of the steel and which are present either intentionally or as impurities. It is quite to be expected and, it is a fact, that the quality of the ilnished steel is innuenced to an important extent by the nature of these reactions and the degree to Awhich they approach' the aa-` commercial steels of otherwise similar composition appears to be related to the variable concentration of these elements in the bath as well as e the form and nature of their compounds which are present in the nished steel, together with the manner of their distribution.

It is the function of a small group of ferroalloys to combine with some'of these common impurities in steel and by their reaction with these elements either to form stable insoluble compounds with them or in some other manner deactivate or fix them and thus eliminate or limit their detrimental effects on the properties of thev finished material. The reaction products may be removed inthe slag or remain behind in the metal as inert inclusions. Y The common deoxidation of steel by means of aluminum or alloys of manganese, silicon, etc., as well as the effect of ferromanganese additions in fixing sulphur in steel, serve as illustrations of this use of ferro-alloys.

The second function of ferro-alloys may, therefore, be considered as a deactivating or scavenging- (a) The art of alloying (b) The art of processing or scavenging In the art of alloying, the addition of an alloying element to the specified composition of the steel is the aim; whereas in the art of processing, the important thing is the reaction of the added elements with the impurities of the steel bath and the effective removal or deactivation of some offending element.

The distinction between these two types of ferro-alloys is perhaps more clearly appreciated when We examine the quite different considerations upon which their respective composition specifications and manner of use are based.

Since the purpose of an additional alloy is simply to serve as a means of introducing one or more of its elements into the composition of a steel base, no greater diiiiculty is experienced in arriving at one or even many specifications of an alloy of the usual steel making elements which will suitably accomplish this aim. In general, it is sufficient that :the alloy contain a substantial amount of the desired element, that it be free from impurities in harmful amounts and that its physical characteristics. i. e., specific gravity,

melting point and solubility are such that it will be readily absorbed by the molten steel bath. Usually the alloy may be added at any convenient time during the steel making process.

In contrast `to this, the setting up of suitable specifications for the composition, manufacture and use of reaction or process alloys, particularly those containing more than one active element, is a problem of a much higher order of `complexity. Here since the alloy is to enter into a set of quite complicatedphysical and chemical reactions with one or more of the constituents of the steel bath and because these reactions must proceed to end points which results in some favorable fixation or removal of these constituents, it is evident that their behavior is a problem of physical chemistry.

Specifications for reaction alloys presume the consideration, not only of the energy changes or so-called driving forces of the chemical reactions which take place between the elements of the alloy and the constituents of the bath, andthe equilibrium or limiting states towards which these reactions progress but also the solubilities, melting points, viscosities, thermal capacities, crystalline habits, surface tension and colloidal behavior of the slag products of these reactions.

All of the phenomena which we associate with chemical amnities, mass action," reaction rates, free energy," "equilibrium" and the other terms of thermo-chemistry and thermo-dynamics become important factors in determining the efliciency of the alloy. It is not sulcient that the elements be simply present in the bath; they must also be present in the right form at the right time, andin the proper concentrations, both with respect to each other and with respect to the other elements of the bath.

This subdivision of ferro-alloys into addition alloys and reaction alloys is not a precise one, inasmuch as certain commercial alloys serve to some degree, both purposes. For example, the value of ferro-manganese to the steel maker is as much for its action on the steel ybath in deoxidation and the deactivation or fixing or sulphur as it is for its suitability for` supplying the manganese content of manganese steels. However, this classiiication based, as it is, both upon the function which the alloy serves as well as upon certain distinctive'chemical features of the alloy itself, is a natural one from the alloy makers point of view,

and will, I believe, serve a useful purpose in clarifying the nature and objects of my invention.

'I'he alloys of my invention are essentially process or reaction alloys both because their more valuable effects on steel quality are the result of physical and chemical reactions which they bring of their composition specifications, together with the manner in which they are used.

My alloys are particularly valuable in flxing the limits of that behavior of steel which is influenced by the presence of the gases, oxygen and nitrogen, particularly the latter.

The gases ioxygen and nitrogen are present in practically all commercial made steels in quantities which are sufficient to have an important influence on the properties of the steel, particularly those properties which determine the steels response to mechanical and thermal treatment They may be present as molecular gas in blowholes or other internal cavities in the steel, in solid solution in the steel, or in the form of nonmetalliccompounds such as nitrldes, oxides or silicates and the like, which may be in solution or exist as inert particles scattered through the steel. The presence of oxygen is believed to affxect the solubility of carbon in austenite and ferrite and thereby to influence such properties as strength, hardness, ductility, elastic limit, impact resistance, etc. Nitrogen is also believed to affect the hardness, ductility, tensile strength, elastic limit, impact strength and magnetic propertiesjof steel and to be a cause for many ofthe phenomena connected with blue brittleness, temper brittleness. age hardness and other allied properties. Also certain phenomena connected with the presence of ghost lines, hair cracks, bands, tendency toward caustic embrittlement, irregularity in carburization and heat treatment and response to nitrogen case hardening (by molten cyanide bath or dry ammonia gas method, etc.) are considerably influenced in one way or another by these gases. Itis, therefore, apparent that the presence of oxygen or nitrogen in steel in various quantities and conditions may well be the reason for the 'fact that steels of otherwise fixed compositions often fail to respond to thermal or mechanical treatment in the manner expected or to develop their anticipated physical characteristics. In manyvv cases this has been proven to be true. The quantity of oxygen and nitrogen present in the steel is. in most instances, not the decisive factor but .rather the form in which these elements are combined and the manner of theirdistribution throughout the steel, i. e., whether they exist as active soluble bodies or as inert insoluble compounds.

In view of these facts, the control of the action of oxygen and nitrogen is a matter of considerable importance to the steel maker. l'-al'ticularly4 -limits of the carbon, silicon, manganese, sulphur and phosphorus content of a steel may be accomplishedl by comparatively direct methods. It is quite practical and, in fact, common practice to determine (e. g. by means of a rapid chemical analysis) the amounts in which these elements occur in the steel at some convenient time and while the bath is held molten. 'I'he amounts of the respective elements are then brought within their desired specification limits by means of additions to the bath or by further refinement before the steel is poured into molds.

' In the case of oxygen and nitrogen, this direct method is not commercially practical. 'I'here has not been developed as yet a. suitable method of chemical analysis which will determine both the amount and the condition of these gases in the steel with suicient rapidity and accuracy to be of use before the steel is cast.

In general, this problem has beenmet by indirect methods. With the help of careful choice of raw materials and the precise following of details of procedure from the time the charge is placed in the furnace until the ingots have been solidied, the steelmaker strives to bring his product to a more or less xed and known state of deoxidation and denitrogenation and thereby produce a steel lin which the variations in the form and amount of oxygen and nitrogen are held Within adequate limits.

In the case oi oxygen, his eorts are facilitated by proper slag manipulation and the use of various commercial deoxidizers such as aluminum, aluminum-silicon, silicd-manganese and the like alloys. With nitrogen, however, no convenient method has been developed for changing either the amount or the form in which it occurs in steel after the steel has reached the ladle. Even with thegreatest care and closest supervision possible to steel makingconditions, variations occur in the form and amounts of oxygen andv nitrogen to asuillcient extent to produce undesirable and unpredictable changes in steel properties, so that often in the case'of steels which are to be made to close specification limits more than one heat must be made before the physicall property speciilcation requirements oi' the steel are met, thereby adding considerably to the cost of production.

I have found that by the addition of controlled amounts ofv ferro or other alloys of certain predetermined characteristics to a suitably prepared steel bath, as will be hereinafter described, I-am. l

able to control and limit the variability inv those properties of a steel, which variability iscaused by or at least associated with variations in the iorm and quantity of' the nitrogen and oxygen in the steel.

`My invention has two general objects: First, the production of steels having greater uniformity from heat to heat in physical properties and particularly those properties which determine the steels response to the mechanical and thermal treatments required in the production of finished articles, which greater uniformity is obtained at a less cost than by methods heretofore known. Second, the production of steels which possess, after suitable heat treatment,

physical properties and combinations of properties of a relatively-high order 'as compared with the best practice in steels of similar base composition. In these new steels,l the usual tensile properties are not only in themselves of a high order but there may be associated with them,

- after suitable heat treatment, other characteristics such as high toughness values at low temperature, i. e., 25 to 125 F. below zero, adaptabilityto nitrogen case hardening, desirable magnetic and electrical characteristics, greatly increased hardenabilty and other useful properties, as will be described later, which are of value. I accomplish both of these objects by adding to the steel bath, under suitable conditions, an alloy which will combine with and render inactive at least a part of the nitrogen and oxygen of the steel.

The eicacy with which any element combines with any other element under a given set of conditions may be evaluated from the equilibrium constant. which constant can be determined either by means of actual measurement or from free energy and entropy equations of the specific reactions involved. These equations employ many constants and factors which, as yet; have not been determined for the complex conditions which occur in steel making.

. Becalme of this and the fact that'the reactions which occur in steel are, themselves, in many cases unknown, the method of exact calculation is not generally possible. Nor is the method of direct measurement practical. The problem becomes very difficult indeed when there is more than one active element and particularly when these elements are added in the form of an alloy. I have found that I am able. by means of easily derived equations and known chemical data, 'to arrive at constants which are related to and which will permit me toy predict, Within certain practical limits, the behavior of the alloys of my invention with respect to their reactions with oxygen and nitrogen in steel. The-method of derivation of these constants will be more clearly understood with reference to the following tables.

I Q value.

TAnLn I Metal Oxygen Heat ol.' oxide Q0 equivaltet lornlmtion o me per gum oxide Hm 0! Oxide (grams oxygen oxygen Me o formation per 1 gram Q0 Symbol Atomic mol Memetal) "o "I'gTn weight Kg Cab mol K- 16.1 Kg. Onlgl Mc-m Ca 40. 1 CBO 152 0. 399 9. 49 .Mg 24. 3 M50 146. 1 0. 658 9. 13 Sr 87. 6 Sr 140. 8 0. 183 8. 80 -Ba 137. 4 B30 133 0. 116 8. 32 zr o1. 2 zro. .25s. 1 0.351 a o7 U B8. 1 U01 255. 6 0. 134 8. 01 .Al 27. 0 A1301 381 0. 889 7. 95 Ta 180. 9 TMO: 379 0. 133 l 7. 90 Cb 92 9 0h10: 365 0. 258 7. 60 V 51. 0 V10: 350 0. 471 7. 30 Ti 47. 9 T101 219 0. 668 6. 86 Si 1 S101 ZI) 1. 140 6. 25 Mn 54. 9 MnO 96. 5 0. 291 6. 03 Cr 52. 0 CraOx 273 0. 462 5. 69 B 10. 8 B10: M 2. 220 5. 83 Mo 96. 0 M003 131 0. 333 4. 09 W 184. 0 W0; 128 0. 174 4. (l)

Fc 55. 8 FeO 85 0. 287 4. 06

TAM.: II

Metal N Nitrogen equiva- Heat of nitride Heat of nim-ide lent of metal formation per Nitride Melt. pt., formation per (l'msnitrogen l Smm nitrogen Atomic Me.Ny C. mol Me.Ny Del' Zfmetal) M Symbol weight Kg. Calmol-1 1 14'! 14.?

Mea: Kg. CaLri Zr 91.2 82.2 0.154 5.86 Ti 47. 9 80. 3 0. 292 5, 73 U 238. 1 274 0.078 4. 90 V 5l. 0 60 0. 275 4. 28 Cb 92. 9 59 0. 151 4. 22 Ta 180. 9 59. 2 0. 077 4. 2 Mg 24.3 117. 5 0.384 4.20 A1 27. 0 56 0. 518 4.00 Cn 40. 1 110 0. 233 3. 93 Sr 87. 6 93 0. 107 3. 32 Ba 137. 4 S8 0. 068 3. l5 Si 2s. 1 17o o. 665 3. oa B 10. s 31. 5 1. 295 9. 25 Cr 52. 0 29. 8 0. 269 2. 13 Mn 54. 9 57. 8 0. 102 2. 01

Fe 55. 8 Fe4N 2. 6 0. 063 0, 19

-Referring to Table I, column 1 lists various elements Iwhich have a strong affinity for oxygen and which have been used to a greater or less extent in the deoxidation of steel. Column 2 gives the atomic weight of these elements, column 3 the oxide which I believe to be formed from the element under the conditions existing in molten steel. Column 4 gives the heat of oxide formation in kilogram calories per gram molecule of metallic oxide. This is designated as the Column 5 gives the oxygen equivalent of metal, that is the Weight in grams of oxygen that can react with one gram of metal. Column 6 gives the heat of oxide formation per one gram of oxygen. It is designated 'by ho.

The meaning and manner of obtaining these values will be apparent from the following: Let us assume thatl it is desired to .combine oxygen with zirconium. The reaction may be represented by the following equation:

This is an exothermic reaction. 'Ihe figure of 258.1 kg. cal. is shown in column 4 in the line representing the reaction between zirconium and Oxygen'- The k value given in column 5 (oxygen equivalent) is derived as follows: It is evident that according to the above equation, 91.2 grams of zirconium will react with 2X 16 or 32 grams of oxygen to produce 123.2 grams of ZrOz. Therefore, one gram of zirconium will react with 32:91.2=0.351 gram of oxygen. In other words, the oxygen equivalent (k) is equal to 16.11 Me.m

and.16X2 grams of oxygen toform 123.2 grams' of ZrO'.` liberated 258.1 kg. cal. Therefore, the

kg. cal. liberated by reaction of one gram of' oxygen is 258.1"+32=8.07. The ho is, therefore, equal to 16Xn in which n is the vnuirrber of .atoms of oxygen represent the amount of oxygen or nitrogen which would be involved in a reaction with a fixed amount of metal. AIn contrast, the ligure in column 6, lHeat of oxide formation or "Heat of nitride formation," might be called an intensity factor--that is, they are related to the energy liberated under the conditions given and' are to that extent a measure of the intensity of the reaction. It will be noted that in these tables the elements have been listed in the order of decreasing heat of oxide formations and heat.

of nitride formations and this is in accordance with their -observed performance for fixing oxygen and nitrogen in steel. Thus calcium has -a higher heat of oxide formation than magnesium or any of the other metals listed below it and it is an observed fact that calcium is a more powerful deoxidizer than any of the other metals listed. The tables, therefore, show the relative eii'ectiveness of the various elements in combining with oxygen and nitrogen.

The figures from which the oxygen equivalent and the heat of oxide formation are calculated are from standard tables giving the values obtained under the usual standard conditions. They are, therefore, not entirely accurate for the some what different conditions which exist in molten steel and for complete accuracy the values would be somewhat'diierent. However ,'since the use I make of them is more qualitative than quanti-- tative, the exact values which would obtain under actual steel making conditions need not be u sed but the values a's they appear in the tables can be satisfactorily used. For the purposes of the present. invention, I am interested more in the relative values than in the absolute values and the values in the tables are satisfactory for the use I make of them.

It will be observed that the tables give the values obtainedupon reaction of single elements with oxygen and nitrogen. 'I'he use of a single element, however, has some practical disadvantages. For example, magnesium or calcium metal have excellent deoxidizing characteristics and will deoxide steel to an` extraordinary extent. But it is impractical to use these single elements under the conditions with which the steel maker is faced.

They are so light that they tend to float on the metal or on the slag and are so reactive thatv Therefore, in practicing the present invention I prefer to use one or more alloys containing more than one active element, thereby not only attaining a high degree of chemical effectiveness but at the same time overcoming many of the practical objections which exist in the case where single elements are used.

It will be noted from the Tables I and II that the elements do not have the same order of effectiveness for combining with nitrogen as for combining with oxygen and that one element may be excellent for one purpose and not very effective for another purpose. Since the usual steel baths contain both oxygen and nitrogen, and since the manner in which both these elements are introduced into steel and removed from steel are interrelated, the reaction alloys of my invention contain elements which are effective for the xation of both these elements. Among the preferred elements are zirconium, titanium, uranium, aluminum, magnesium, calicium, barium, strontium and vanadium. Since it is an important function of my alloy to combine with and deactivate the nitrogen in steel, itis essential that it contain an element or elements suited to do this to a lhigh degree. Such elements, for example, are zirconium, titanium and uranium. Further, since the removal of nitrogen and oxygen are closely related, I also employ an element or elements having strong a'lnity for oxygen, such elements being, for example, .the alkaline earth metals calcium, barium and strontium, and magnesium and aluminum.

My reaction alloy always contains zirconium or titanium or uranium or a combination of these elements, because of their nitrogen xing char acteristics. In addition to the nitrogen xing elements, it is preferable that the alloy contain one or more elements which have a greater affinity for oxygen than have the titanium, zirconium or uranium. The preferred elements for combining with oxygen are calcium, barium, strontium, magthe major part of the addition burns in the air or combines with the slag rather than reactingv with the oxygen in the metal. The same objection is also true to some extent in thecase of aluminum. Also when aluminum Valone is added to a steel bath, its reaction products are in nely divided form and as the amount of aluminum added is increased, the size of the reaction product particle decreases and true suspensions appreaching the colloidal may be formed in the steel if the steel is treated with an excess of metallic aluminum. This behavior of aluminum, which is also the case with titanium and some other single elements is detrimental to some of the properties o! the steel.

nesium and aluminum. Where the alloy contains both titanium and zirconium or both titanium and uranium,` the zirconium or uranium, since they have higher heats of oxide formation than titanium may loe used in place of or in addition to the calcium, barium, strontium, magnesium or aluminum. Although it is possible to accomplish the removal of oxygen by the use of a separate deoxidizer, it is preferable that the reaction alloy of my invention contain both a nitrogen flxing 1. Activeelements i 2. Auxiliary elements The active elements are those which combine with oxygen or nitrogen or both oxygen and nitrogen, under the conditions prevailing in a steel bath to form stable non-reactive products. The preferred active elements are titanium, zirconium,A aluminum, magnesium, calcium, strontium.

The auxiliary elements are not indispensable but they are useful either in imparting certain desirable Properties to the alloy or rendering the processof manufacture of the alloy easier or are necessarily present under the commercial conditions of manufacture. The auxiliary elements are of three classes-i. e.:

(a) Carrierelements (b) Modifying elements (c) Subversive elements 'I'he function of the carrier element or elements is to serve as a vehicle for introducing the active elements into the bath to be treated. The usual carrier element ls iron, although I may use nickel, copper, cobalt, manganese or other suitable metal which does not materially interfere with the reactions of the active elements.

In general, the modifying elements are used to assist in giving the alloy suitable specific gravity, melting point, solubility and other essential physical properties which facilitate its manufacture or use or which further improve the form, size or distribution of the reaction products. They may also protect the active elements in their function of deactivating nitrogen and oxygen. The preferred modifying elements are tantalum, tungsten and molybdenum. Manganeseis also a deisrable modifying element in increasing theeffectiveness of the alloy particularly where the alloy contains substantial amounts of carbon and/ or silicon. It is generally used in amounts of theR order of 5 to 2l)%.

The subversivev elements are those which render the alloy less active but which are present to a greater or less extent, due to the process of manufacture of the alloy or to the ingredients employed. The effect of these undesirable elements will be described more in detail hereinafter. I have previously described how the heat of oxide formation, the oxygen equivalent, the heat of nitride formation andthe nitrogen equivalent are obtained when only a single element reacts, and I have stated that these figures may be used as a measure of the ability of the elements to react with oxygen and nitrogen. I have also stated that the reaction alloys of the present invention preferably contain several elements for reacting with the oxygen or nitrogen rather than a single element. I have observed that the action of an alloy of two or more elements which lwill react with oxygen and nitrogen yunder the conditions prevailing in a steel bath is different than if these elements-Were added separately.

Although the chemical reactions included in using an alloy of several elements are very com.. plex, I may, however,- by a simple calculation arrive at figures which I have found to be adequate criteria for determining the chemical suitability or unsuitability of the alloy as a reaction alloy for treating steel in accordance with this invention. These figures are the average heat ci' oxide formation, average heat of nitride formation, the

oxygen equivalent and the nitrogen equivalent when such figures are calculated on the basis of the percentages of active elements in their active form The average heat of oxide formation and average heat of nitride formation of an alloy containing more than one Vactive element may be calculated as follows:

The alloy is characterized by four figures, two for each of both deoxldation and denitrogenation, and are Om and Nm, which are the oxygen and nitrogen equivalents respectively, and Hi and u Hi, which are the average heat of oxide and nitride formation respectively:

`(A) Omo and N100. oxygen (nitrogen) equivalent,

in grams, of the active metals in grams of the alloy. These figures are calculated from the equations:

I Bielli u B/eulu' In lVlenLIul mr, mu, mm, and nr, nn, nm, (xr, xn,

mm, and y1, im, ym, are the number of metal atoms and oxygen (nitrogen) atoms, respectivelyfin one molecule MemOn (MerNy) of the oxides (nitrides), formed in deoxidation (denitrogenation), of the active metals I, II, III, of the alloy.

Mer, Meu, Mem in the equations showing the values of kr, kn and km, represent the atomic weights of the active metals,

(Mer), (Men), (Mem) in Equations l to 6,

represent their'percentages in the alloy.

(B) H1" and HiN the average heat, in kg. calories, of oxide (nitride) formation for 1 gram of oxygen (nitrogen), (whereby all active metals are assumed to take part simultaneously and in the proportion in which they are contained in the alloy) H1"v (and HiN) is obtained by dividing H1000 (HionN), which represents the total of heats, developed when each of the active metals in 100 grams of the alloy forms its oXide (nitride), by 0100 (N100) I HMO:

Applying this general formula to a specific alloy, let us assume that the composition of the alloy is 20%, titanium, 20% aluminum, 7% zirconium,f2.9% silicon, balance essentially iron. Substituting the numerical values in Equation 1 to 'determine the oxygen equivalent, we have:

Substituting numerical values in Equation 2 to determine the nitrogen equivalent, we have:

Substituting the numerical values in Equation 3, we have the heat of oxide formation in kg. cal.

per 100 grams of the alloy, giving a value of 273.0

Substituting the numerical values in Equation 4, we have the heat of nitride formation in kg. cal. per 100 grams ofthe alloy, giving a value of 87.0 kg. cal.

EQUArxoN 4a 0.154X 5.86 X 'i4-0.665 X 3.03 X2.9=87.0 kg. cal.

Substituting the numerical values in Equation' 5, we have the heat of oxide formation in kg. cal.

per gram of oiw'gen '1.39 kg. cal.

I EQUArxon 5a Hmwao: i

om 7.39 kg. cal.

n Substituting the numerical values in Equation 6 to determine the average heat of nitride fox-mation, we have Equation 6a, giving a value of 4.53

Equation 6a Iig-ENlL-g-g-isa kg. cal.-

,These four iigures, together with other information, as will be explained, may be usedl within 'limitato predict the behavior of the alloyl when added to steel for the purpose of deoxidation and denitrogenation.

I have said that in the calculation of the average heat of oxide and nitride formation and the oxygen and nitrogen equivalent, the gures, are

calculated on the basis of the percentages of theactive elements. By this I mean we consider those elements as active which will react with either oxygen or nitrogen under the conditions prevailing in the steel. Thus, although not limited to such elements, all elements having a' In general, manganese is not to vbe calculated as an active element.

Special consideration must be given to the elements carbon and silicon, inasmuch as they may form stable compounds, i. e., carbides and silicides with some of the active elements (titanium, zirconium, calcium, barium, strontium) 4of a higher order of stability than the other alloy combinations which may be formed between the active elements. My alloy does not contain over 5% carbon. Itis preferred that carbon be not over 2% or better still, not over 1%.

As pointed out previously, infarriving at the average heats of oxide formation and nitride formation of an alloy, I consider only that portion of each active element which is in active form. I shall now discuss wiiat is meant by active form. I have pointed out that the formulae are valuable because the figures obtained from them are related to the energy available in the alloy and which determines the driving force with which the alloy will combine with oxygen and nitrogen. From the point of view of available energy, the ultimate analysis oran alloy of several active constituents is not a true indication oxygen and nitrogen. There must be takeninto -of the eii'ectiveness of the alloy in removing;

consideration the form in which the elements of the alloy exist and particularly the possibility ofYY compounds existing between thedifferent elements'of the alloy which may'greatiy iniluence the amount of available energy. For example, if carbon is present in an alloy containing titanium, such car-bon will generally be combined with the titanium as titanium carbide and an alloy in which the titanium exists as titanium carbide has been found to act with less emciency in the removal of oxygen and nitrogen than would an alloy having the same amount of titanium in uncombined form. In a similar manner, silicon combines with, for example, any of the strongly basic elements such as calcium, barium, strontium, sodium and potassium to form silicides. I have found that an alloy in which the calcium exists as calcium silicide is less effective in the removal 'of oxygen from steel than when the calcium exists in uncombined form. Neither titanium carbide-nor calcium silicide are subversive of the reaction characteristics of the alloy. In fact, they are helpful but are not as effective as the titanium and calcium. The following examples will illustrate further what is Balance any one or more of iron, nickel, copmeant by the portion of each active element which is in active form. In Example A, the alloy contains:

Per cent zirconium 15 Titanium 20 Aluminum 10 Calcium 4 Silicon 8 Carbon 4 per, cobalt or manganese.

The active elements in this alloy are zirconium, titanium, aluminum, calcium and silicon, since each of them has a heat of oxide formation of 6.0 or over or a heat of nitride formation of 4.0 or over. In calculating the heat of oxide formation and heat of nitride formation, however, we do not take the full percentages of all of the elements, because certain' portions of 'these elements have been converted into less active form. I'he 4% of carbon in the alloy may be combined with approximately 16% of titanium to form titanium carbide, thereby leaving approximately 4% of active titanium. The 4% of calcium may be combined with about 5.6% of silicon to form calcium silicide (Ca'Siz), leaving about 2.4% of silicon in active form. Accordingly the percentages of ac- These are the percentages which are used in the formulae above referred to.

In arriving at the percentages of active elements in active form in an alloy, the carbon must 6 always be taken into consideration, since, as

pointed out above, it will form carbide with titanium. Carbon will also form zirconium carbide, as well as carbides with vanadium, molybdenum, tungsten and other strong carbide forming elements, but in the above examples we have assumed thatit forms only titanium carbide. As pointed out in connection with Example A, calcium and'silicon will form calcium silicide. Likewise silicon will vreact'to form the silicides of barium and strontium. Therefore, if the reaction alloy contains silicon and any strongly basic element such as calcium, barium, stron tium, sodium or potassium, we assume for purposes of calculation that the alloy contains the silicides of these elements and the silicon in active form is calculated as described for Example A. It will be noted, however, that in Example B the alloy does not contain any strongly basic element and, therefore, all of the silicon is considered to be in active f orm.

Below is given Table III, which gives the chemical compositions of four alloys. the heat of nitride formation, the nitrogen equivalent, the

tive elements of the alloy which are in active form are:

Per cent Zirconium 15 Titanium 4 Aluminum l0 Silicon 2.4

These are the values which are used in Formulae 1, 2,'5 and 6 in determining the oxygen and nitrogen equivalents and the heats of oxide and nitride formation'and the values expressed in the claims -are determined in the manner described.

Consider as another example a reaction alloy as follows: EXAMPLE B Per cent zirconium 15 Titanium 20 Aluminum 10 Silicon 8 Carbon 4 Balance any one or more of iron, nickel, copper, cobalt or manganese.

It win be noted that reaction auoy n 1s similar to reaction alloy A, except that alloy B does not contain calcium.

Considering now alloy B, .the 4%of carbon may be combined with about. 16% of titanium to form titanium carbide, leaving in the alloy about 4% of titanium in active form. 'I'he percentages of active elements which are in active form accordingly are:

` Per cent zirconium l5 Titanium 4 Aluminum 10 Silicon 8 Tnx.: III

N Kg. O Kg. V 'r1 A1 zr si ioo G. Cal. 100 G A Cn.

alloy GM N Gm 0 18.2 9.3 as 1&9 L50 35.5 7.10 15. 6 10 a 3. 3 17 4. 46 32 7. 22 21. 5 10.7 3. 2 17. 6 4. 56 33. 9 7. 17 20 20 7.07 2.90 19.26 4.53 31.1 7.38'

^ heat of oxide formation and oxygen equivalent calculated according to the method described.

It will be seen that the alloys are all similar with respect to theheats of oxide and nitride formation, as well as their oxygen and nitrogen equivalents, although they are of widely different chemical composition. l

It will be noted from this table that the heats of oxide formation and-nitride formation (which Per cent Carbon .41 Manganese 1.75 Vanadium l None- Sihmn' 0.23

7 lPiumini-ua'. .02o Sulphur .018 Aluminum .028 Active nitrogen .0082

The chemical analyses o: the-verm moa are measures of the intensity of deoxidation and after treatment with the different reaction alloys were:

High tensile bars were forged to 1116" rd., nor'- Insot f malized at 1600 F. (1 hr.), cooled in mica, then machined to .5201 rd., hardened at 1550 F. (1

1 2 3 4 hr.), oil quenched, drawn at 450 F. (2 hr.) and C b ground. Low tensile bars were forged to 1115 rd.

1 323 g 1,325 113,... drawn at 900 F. (2 hr, then machined and Mulflz-n :82g :ggg fg 02%@ .l0 ground. Low and high drawn Izod impact bars Active nitrogen... ,0015 .0016 0017 .0007 wereprocessed 1n the same manner as the tensile bars. Hardenabillty bars were forged to 11/4 'The silicon, phosphorus and sulphur were substantially the same as in the untreated steel.

The figures given for Active nitrogen represent that part of the nitrogen. whichv is soluble Two bars from the middle of each of the treated ingots were rolled to 1%" rd.

rd., normalized at 1600 F. (1 hr.), mica cooled, machined and treated per Jominy test at 1550 F. (1 hr.), water cooled. The results of these tests are appended in the table below.

TABLE IV Alloy addztzons Plain steel (l) (2) (3) (4) High tensile bar-450 F. draw:

Yield point 238, 60G-236, 600 247, OOO-248, 850 '246, 200-247, S50 243, 650-243, 200 247, 15G-246, 600 Ultimate.. 250, 800-251, 450 269, BOO-269, 200 266, S50-266, 270, 950271, 100 270, 20G-271. 100 Elong. 2" 9. 5-10. 0 13. 5-13. 5 12. 0-13. 0 13. 0-13. 0 13. 0-13. 5 Red. area 33. 15x34. 80 51. 20-50. 95 52. 60-52. 05 49.00-50.40 50. iO-51.50 P" value. 89. 94-92. 05 115. 36414. 98 116. 39-115. 70 112. 99-114. 70 114. 52-116. 02 Izod im act.. 5. 21.8 19.7 17.0 22.3 Low tensile lar-900 F. draw:

Yield point 161, 400-161, 500 162, 500-161, 500 157, 350-157, 900 153, 700-151, 650 Ultimate 145, 700-140, 100 169, OOO-169, 700 164, 300-164, 900 165, 950-166, 050 162, 000-161, 150 Elong. 2" 17. 0l6.0 16. 0-16. 0 16. 0-16. 5 16. 0-17. 0 18. 0-18. 5 Red. area 56.10-58. 65 54. 75-54. 50 56. 60-55. 30 56. 35-57. 15 57. 40-57. 65 "1" value 96. 46-98. 40 99. 50-99. 34 100. 78-99. 34 100. 81-101. 79 101. 28-101. 41 Izod impact 7217 48. 6 58. 7 50. 1 55Y 9 Hardenability, (Jominy test): l

Hc 57' i 58 ,58 59 58 57 58 57 58 57 64 57 56 57 57 40 56 56 56 56 41 56 56 56 55 36 56 55 56 55 33 55 55 55 54 31 55 54 55 52 30 55 53 55 51 26 53 48 52 40 24 46 38 44 32 22 36 32 33 28 in the steel (for example iron nitride and silicon nitride) and which goes into solution and appears in the filtrate when the steel sample to be analyzed is dissolved in dilute hydrochloric. acid. The concentration of the acid used in preparing the steel for active nitrogen analysis should be such that the nitrides relatively insoluble in steel and which exist as small inert particles in the form of inclusions (e. g. titanium nitride and zirconium nitride) are not attacked and appear as a resi-n due.

An example of a method of determining the active nitrogen content of a steel is as follows: 20 gms. of sample were placed in a 400 m1. beaker and ml. of Water added. Ten m1, of concentrated HC1 was added and when the vigorous action ceased an additional 10 ml. was added. this was continued until a total of 70 ml. had been added. At the end of the acid addition heat was applied gently until all gas evolution had ceased. The samples were then ltered and washed with hot 1% 'HC1 solution. The nitrogen in the ltrates was then determined.

.The total nitrogen content of each cf the steels was closely alike'and of the order cf .007%. It will be noted, however, that while in the untreated steel almost all of the nitrogen (.0062%) was in active and soluble form, vin the case of steels 1, 2, 3 and 4 which had been treated with the alloys of my invention the soluble nitrides were greatly reduced to the order of `.00l5% and the i greater part. of the nitrogen content of the steels was1 converted into the inert and insoluble form.

It will be noted from Table III that the heat of oxide formation of the alloys is in all cases over 7.0 and that the heat of nitride formation is in all cases over 4.25. Table IV shows that the steels produced by use of the various reaction alloys were all improved to a. similar degreein all of the properties measured. This indicates that so far as the chemical adequacy of the various alloys is concerned, the heat of oxide formation and heat of nitridev formation and the oxygen and nitrogen equivalents are important criteria in determining beforehand the suitability of a reaction alloy in improving the physical properties of steel treated with the alloy. Furthermore, that alloys of my invention having heat` values of the same order will produce in steel physical properties of the same order, even though the alloys may vary widely in chemical composition.

It will be seen from Table IV that steels which have .been treated with small amounts of the reaction alloys have properties which are greatly superior to the untreated steel. Considering the high tensile bars from the treated ingots, which bars were hardened at 1550 F., quenched in oil and drawn at 450 F., it will be seen that they have yield points of approximately 245,000 pounds per square inch, as compared to 238,600 pounds per square inch for the untreated steel. The ultimate tensile strength for the treated steels is of the order of 267,000 pounds per square inch,

as compared with 250,000 pounds per square inch for the untreated steel. The elongation for the 5 treated steels is of the order of 13% as compared with 10% for the untreated steel. The reduction in area for the treated steels is of the order of 50%, as compared to 33% for the untreated steel. The P value, which is a merit number, is of the order of 114 for the treated steel, as compared to 90 for the untreated steel. The Izod impact value for the trted steel is of the order of 19 foot-pounds, as compared to 5.5 foot-pounds for the untreated steel.

The hardenability as shown by the Jominy test of the treated steels is greatly superior to that of the untreated steel. The range of hardenability for the untreated steel is from 57 Rockwell C hardness at 11g" to 22 Rockwell C hardness at 3", whereas the hardenability of the treated steels ranges from about 58 Rockwell C hardness at 11g" down to about 28 Rockwell C at 3". What is more important, however, is the fact that all of the treated steels have a Rockwell C hardness of at least 50 at l", whereas the untreated steel hardened to 50 Rockwell C for only a distance of Mi. It will be evident, therefore, that since the position in inches from the quenched end ofthe J ominy bar at which the hardness is 50 Rockwell C is much greater in the case of the treated steels than for the untreated steel, and since these positions are a measure of cooling rates, it follows that a treated steel may be use d in much heavier In addition to the physical characteristics above noted, treated steels made according to my invention show other remarkable properties, among which is their high impact values, at their high hardness values, at low temperatures.

For example, two samples of steel each having a composition similar to the untreated steel given in Table IV-i. e., carbon about .40% and menganese about 1.70%, were prepared. One of the steels was treated by adding alloy in the amount of four pounds per ton, whereas the other steel was untreated. These two steels were normalized at 1625" F., quenched in oil from 1525 F., and subsequently drawn at 450 F. and cooled in airand tested for impact values by the Charpy method and for hardness by the Vickers Diamond Brinell method and the Rockwell method. The results are shown in the following tables:

Untreated steel It will be appreciated that a steel of this chemical composition and hardness which has an impact value of 17 foot-pounds at 90 F. is very remarkable. 1

I have found further that steels which have been treated by the addition of small amounts of reaction alloy are much superior to untreated kept below harmful limits.

Percent Carbon .40 Manganese 1.70 Silicon .20 Sulphur .03 Phosphorus .03

were heated in a liquid cyanide bath at a temperature of about 1550 to 1575 F. for about 40 minutes, and then quenched in oil and drawn at 450 F. and subjected to destructive tests. Gears of similar composition, except that the steel had been treated with reaction alloy in the amount of four pounds per ton, were also treated and tested under similar conditions. The life of the gears made from the reaction alloy treated steels as determined by excessive pitting and breakage was from 30 to 40 hours, as compared to a similar life or 5 to 15 hours for the gears made from the untreated steel. Microscopic examination of nitrided steels made from steels which have been treated with reaction alloy show a deeper penetration of the hardening gases, that is a deeper nitrided case than those produced from untreated steels.

I have furtherfound that the magnetic properties of steels, for example permeability and coercive force, are changed to a marked degree by the addition of reaction alloy to the steels.

As I have pointed out previously, there are other factors which must be taken into consideration in addition to the chemical adequacy of the alloy as indicated by its heat values.

1. 'I'he alloy should contain a minimum of those elements which are harmful to the intended reaction, or should contain some element or elements which compensate at least in part for the detrimental eiects of such harmful elements,

if present. Since the ability of the alloy to deactivate oxygen and nitrogen is primarily a question of available energy, any element which combines with the nitrogenor oxygen-xing elements to form intermetallic compounds and thereby reduces the available energy of the alloy for deoxidation or denitrogenation is undesirable. Also any element which will form soluble (active) nitrides in the iron or steel should be In both of these respects, silicon is a serious oiender and my alloys are essentially low silicon alloys or contain 'some corrective element.

2. The alloy should have a physical form suited to normal steel making processes-i. e., its melting point, solubility, speciilc gravity. density, etc. should be such that it may be added to the ladle or molten stream and be rapidly absorbed by the steel with little loss. For example, alloys which are of too low speciilegravity will float adequate for the deoxidation of steel but it is quite impractical to use this material for such purpose.

3. 'I'he residual elements of the alloys remaining in the steel after the i'econ shouldbe beneasmase due to the nature and distribution of the alu--l mina, many disagreeable qualities affecting grain size, banding, carbon diffusion rate, etc. appear. In the case of a steel treated with titanium alone. under certain circumstances the bath is extremely sluggish and I attribute this to the presence of the by-products of the reaction in any unfavorable condition.` In compounding my alloy, I therefore choose the combinations of elements to as great extent as possible which will form by-products which melt at a lower temperature than prevails in the steel, thereby insuring some coagulation and a size of lay-product which is not detrimental to the reaction.

5. The alloy should be low in cost-,that is, readily made from low cost ores.

A preferred alloy according to my invention contains:

Percent Titanium About 20 Aluminum About 20 zirconium About 7 Balance substantially all iron.

The active silicon is less than 15% and preferably less than 10% or, better still, less than 5%. The primaryI purpose of the alloy is to deactivate nitrogen in steel, although it is also important that it have the ability to deoxidize the steel. In this preferred alloy, titanium is used as the principal nitride forming element. It will be noted from Table II that titanium has a very high heat of nitride formation (5.73). Furthermore, titanium nitride is relatively insoluble in steel.

Under actual steel making conditions, it is almost invariably the case that the steel also contains oxygen. If the steel were free from oxygen or were not subject to reoxidation or renitrilca' tion from the air after treatment, I might use titanium alone for the purpose of removing the nitrogen. Although a low carbonl ferro-titanium might be effective in removing nitrogen from steel, it is not very effective under actual steel making operations. because the titanium reacts with the oxygen before it has a chance to react with the nitrogen.. and, therefore, its effect in reducing the active nitrogen content of the steel is lowered. Therefore, the Yalloy should contain a deoxidizer which is more powerful than the titanium. As deoxidizers, I may use one or more of the elements aluminum, magnesium, strontium. barium or calcium, the preferred deoxidlzers being aluminum or magnesium. It will be noted from Table I that aluminum and magnesium each has a higher heat of oxide formation than does titanium and, therefore, they are effective in removing oxygen, thereby saving the titanium` for its function of removing nitrogen.

Although an alloy containing titanium andaluminum is suitable for some purposes, it is improved by the addition of zirconium. It is pref ferred, therefore, that a portion of the titanium of the ferro-titanium aluminum alloy be substituted by zirconium, inasmuch as I am thereby able to raise the heat of oxide formation and maintain a high heat of nitride formation. In other Words, the ability of the'alloy to remove oxygen is'increased, because of the substitution of a part of the titanium by. zirconium. The presence of zirconium also improves the form, size and distribution of the reaction products. The pre-` ferredalloy, therefore, contains titanium, aluminum and zirconium in proportions such that the titanium is higher than the zirconium.

In some cases, however, the alloy may contain zirconium in greater amount than titaniumthat is, the alloy may contain zirconium, aluminum and titanium in which the zirconium is greater than the titanium. Considering two alloys each containing titanium, zirconium and aluminum, the rst containing more titanium than zirconium and the second containing more zirconium than titanium, the total of titanium and zirconium being equal in both cases, the rst alloy Will have a higher oxygen equivalent and a higher nitrogen equivalent than the second alloy. That is, the capacity of the first alloy to combine with oxygen and nitrogen is greater than that of the second alloy. On the other hand, the heat of oxide formation and the heat of nitride formation of the second alloy is greater than that of the rst. In other words, the intensity with which the alloy combines with nitrogen is greater for the second alloythan for the rst. The alloy may, therefore, contain more titanium than zirconium or more zirconium than titanium, depending upon the particular conditions `under which it is desired to use it. However, for most purposes, I- prefer the alloy to have higher tita nium than zirconium because in an alloy having a suiiiciently high intensity factor (heat of nitride formation and heat of oxide formation), it is usually advisable to have a high capacity for ,removing nitrogen and oxygen.

The incorporation in the 'alloy containing titanium or zirconium or both titanium and zirconium and also aluminum or other strong deoxidizing element, of a strong carbide forming element, further increases the effectiveness of the alloy under some conditions. Thus alloys containing titanium and aluminum or zirconium and aluminum may advantageously include one or more carbide forming elements such as tantalum, uranium, molybdenum, tungsten or chromium. The

preferred carbide forming element is tantalum.

'I'he incorporation of carbide forming elements decreases theV tendency of thetitanium or zirconium to form carbides and thereby leaves them available for reacting with the nitrogen. The carbide forming elements, therefore, act as protecting agents for the nitrogen fixing elements titanium and zirconium, and, in general, improve the density, specific gravity andy melting point and other desirable characteristics of the alloy. Tantalum is'a particularly useful carbide forming element because it has high heats of oxygen and nitrogen formation and high oxygen and nitrogen equivalents. It may, therefore, be used in relatively large or small amount without unduly altering the heat values of the alloy.

In my alloy, the active ingredients are always used in such proportion as to produce an alloy having an average heat of oxide formation per gram of oxygen of at least '7 kg. cal., `preferably at least '7.10, and a heat of nitride formation' per gram of nitrogen .of at least 4.25, preferably at least 4.50, when these values are obtained by the Formulae 5 and 6, using the values given in Tables-I and II for the constants involved and considering only the active elements in their active form.

The amount of oxygen and nitrogen which can be combined with a given amount ofalloy is a function of its oxygen and nitrogen equivalent of the alloy. My alloy has an oxygen equivalent of at least grams of oxygen per 100 grams of alloy and preferably has an oxygen equivalent of at least 30 grams of oxygen per 100 grams of alloy, The alloy has a nitrogen equivalent of at least 5 grams of nitrogen per 100 grams of alloy and preferably has a nitrogen equivalent of at least grams of nitrogen per 100 grams of alloy. An alloy having an oxygen equivalent of about 30 and a nitrogen equivalent of about 15 is generally used in an amount of about four pounds per ton in treating open hearth steels.

The alloy preferably contains:

Percent Titanium About 10-30 Aluminum About 10-30 Zirconium About 2-12 Balance substantially all iron.

. would have substantially the same eect in deoxidizing and denitrogenizi'ng a steel bath, except that it could be used in amount of only V2 that which would be required if an alloy were used containing titanium, 20% aluminum, and '7% zirconium. Similarly an alloy centaine ing 10% titanium, 10% aluminum and 3.5% zirconium would produce substantially the same effects but would have to be used in twice the amount of an alloy containing 20% titanium, 20% aluminum and '1% zirconium. I do not mean by this, however, that this type of dilution is of no importance, because it is often desirable to have the actual contents of the active elements in an alloy within certain given ranges, in order to produce an alloy having suitable specific gravity, melting point and other physical properties and the efnciency of the alloy is, to a considerable extent, a function of the state of dilution of the active elements in the alloy.

Although the titanium, aluminum and zirconium are preferably within the ranges above given, the ranges of these elements may be somewhat broader. The alloy may contain titanium from about 2 to 65%, aluminum from about 2 to and zirconium from about 2 to 65%.

From the standpoint of the effect of the reaction alloy on deoxidizing and denitrogenizing steel, the presence of silicon is definitely detrimental. Its low heat of oxide formation and lowV heat of nitride formation lower the average heat of oxide and nitride formation of the alloy and thereby render it less effective. Secondly, silicon forms inter-metallic compounds with some of the principal active elements of the bath, such as calcium, barium or strontium and thereby reduces the available energy of those elements for deoxidation and denitrogenation. Thirdly, silicon forms a nitride which is soluble in steel.v

Referring to the harmful eiect of silicon in forming soluble nitrides in steel, it is the amount Y'that the active Saucen of silicon in active form. It is only the silicon which is in active form which is harmful in forming the soluble nitrides and which should, therefore, be kept low in amount. In my alloy, the active silicon is not more than 15%, preferably less than 10%, and better still is less than 5%. It is desired to keep the silicon as low as possible but my alloy may contain small amounts of silicon, because such alloy is easier or more economical to produce than one not containing silicon.

It also is preferred that the carbon in my alloy ybe as low as possible. The carbon should not be over about 5% and generally is under about 2%. The carbon combines with titanium and zirconium, thereby using up a portion of the titanium or zirconium which would otherwise be available for fixing nitrogen. Due to the difference' in atomic weights between carbon and titanium and zirconium, even relatively small amounts of carbon in the alloy will combine with relatively large amounts of titanium and zirconium, thereby considerably reducing the effectiveness of the alloy for deactivating nitrogen.

Although it is preferred that the alloy contain both titanium and zirconium and also aluminuml it may contain only titanium and aluminum or zirconium and aluminum. The alloy may contain titanium or zirconium or both titanium and zirconium in amount between about 2 and 65%, aluminum or magnesium or a combinationA of aluminum and magnesium in amount of about 2 to 50%. In any of the alloys, the aluminum may be replaced either partially or totally by magnesium;

Although aluminum and magnesium are the preferred deoxidizers, I may replace either or both of them in whole or in part by one or more of the elements barium, calcium or strontium.

-from about"2% to 65%, preferably between 10 and 30%. The aluminum may be from 2% to 50%, although it usually is at least 5%. Preferably the aluminum is between about l0 and 30%. The zirconium is from about 2% to 65%, preferably from about 2% to 12%. Where the alloy contains both titanium and zirconium, the sum of the titanium and zirconium does not exceed Carbon and silicon are subversive elements and are kept low. 'I'he carbon is not over about 5% and preferably is not over about 2% or better still it is not over about 1%. The total silicon in the alloy is not over about 30%. The active silicon is in no case over about 15% and is preferably not over 10%. It is still more preferable bf. not over about 5%.

. present inthe alloy the sum of them, should amount to about to 30%. They should be present in quantities sufdcient so that they will react with the silicon in the alloy and leave not over about 15% of silicon in active form. Preferably the active silicon should be less than or, better still, less than 5%.

'Ihe modifying elements tantalum, uranium' molybdenum tungsten and manganese should be present in the alloy in the total amount ranging from an eiective amount up to about 40%. An effective amount usually is in the neighborhood of 2% or more.

The balance of the alloy, aside from the active elements which have been referred to, is usually iron. However, my invention is not restricted to ferrous alloys. I may replace iron, either in whole or in part, by one or more of the elements, nickel, manganese, cobalt or copper or other element or elements which are not subversive of the properties of the alloy. The use of these elements may in some cases facilitate the making of the alloy or it may render the alloy more desirable from the standpoint of specific gravity, solubility, melting point and other physical properties, as has been heretofore described.

The invention will be further understood by reference to the ternarydiagrams of Figs. 1, 2, 3 and 4. v

Considering nrst Fig. 1, thisisa ternary diagram illustrating the system titanium, zirconium and aluminum. It will be noted from Tables I and II that the heats of oxide formation and nitride formation of titanium, zirconium. and aluminum are:

Oxide for- Nitride mation formation Titanium 6. 85 5. 73 zirconium 8. 07 5. B6 Aluminum 7. 95l 4. 00

'- centages of these elements in the alloy which is to be added to iron or steel. They are, however, the percentages of these elements when -these yelements are considered as constituting 100%. It will be noted that any combination of these elements lying to theleft of the line 2-3 has a heat of oxide formation (H10) of at least '1.10.` It will be noted further'that any combination lying to the right of the line I-5 has a heat of nitride formation (Hin) of at least 4.50. Accordingly the area l-2-'-34-5 represents combinations in which the Iheat of oxide formation is at least 7.10 and the heat of nitride formation is at least 4.50.

Any combination within'the area I-2-3-I-5, therefore, has satisfactory heat of oxide formation andv heat of nitride formation according to the invention but there are other criteria, as have 'l been referred to herein, which should also be taken into consideration. that the percentages of the zirconium, aluminum 5 and titanium should be such as to fall within the more restricted area 6-1-.8-L-9-I0. I prefer that the composition fall within the 4even more restricted area I l|2|3|4|5|5a. Compositions falling within this smallest area II-IZ--I3--I4-i5-I5a are advantageous for a number of reasons. They have a very high nitrogen equivalent. They are easy to make and have good physical form, good solubility in iron and steel and are of sufliciently low melting point. The products ofreaction of these alloys with oxygen and nitrogen of the steel are of composition, size and melting point such as to produce steel of very satisfactory Qualities.

It 'is quite advantageous that the alloy contain all three of the elements titanium, zirconium and aluminum. If the composition were constituted entirely of titanium and aluminum, as shown by the diagram, the aluminum would have to .lie between 20 and 58% and the titanium between 42 and 80%, in order to give a heat of oxide for'- mation of atleast 7.10 and a heat of nitride formation of at least 4.50. If, however, the composition contains zirconium in addition to the ti- .sion of zirconium in the composition I have a.

wider latitude in varying the proportions of titanium and aluminum, in order to produce compositions which give me -the, other properties which' are desirable in the compositions. A fur ther advantage of usingzirconium as well as titanium as nitrogen xing elements is that the products of reaction are in more favorable form than would ,be the products of reactionof either titanium or zirconium used singly.

' The inclusion of silicon in\a titanium alloy is definitely detrimental, as will be seen by reference to Fig. 2. This figure is a ternary diagram of the system titanium-aluminumsilicon. Com- 5 vpositions within the area IG--Il-l each have a heat of oxide formation of at least 7.0 and a heat of nitride formation of at least 4.25. Compositions within the smaller area l9202i have a heat of oxide formation of .at least 7.10 and a heat of nitride formation of at least 4.50. If the composition contained only titanium and aluminum, the aluminum mi'ght be between 20 and 58% and the titanium between 42 and 80% and the compositions' would each have' a heat of oxide 00 formation of at least '1.10 and, a. heat of nitride formation of at least 4.50. It will be noted, however, that as silicon is included in the composition the range of aluminum and titanium rapidly. decreases and that when there is abovev 13% of silicon, no combination of aluminum, titanium and -silicon will produce a heat of oxide formation of at ieast '1.10 and a, neat of nitride forma- I, therefore, prefer The composition represented by the numeral content than any other ratio of these elements, while still maintaining adequate heat of oxide formation and heat of nitride formation. This is also an advantageous ratio of these elements from the point of view of the melting point of the reaction products.

I prefer that the percentages of these elements titanium, aluminum and silicon in their active form when calculated on the basis that said active elements in active form constitute 100%, fall within the area 40--42-43. Any composition falling within this area has a heat of oxide formation of at least 7.0 and a heat of nitride formation of at least 4.50. I further prefer that the composition be such that it fall within the more restricted area 40-4|-2l. Compositions Within this more restricted area have a heat of oxide formation of at least 7.10 and a heat of nitride formation of at least 4.50. These areas include compositions having the advantageous ratio of titanium to aluminum of approximately 2:1. In general, alloys which have a higher heat of oxide formation, all other characteristics being the same, are superior to those having lower heats of oxide formation.

Fig. 3 represents the system titanium-zirconium-silicon. All compositions falling Within the area 22-23--24 have a heat of oxide formation of at least 7.10 and a heat of nitride formation of at least 4.50. In thisI gure, any composition below the line 25-26 has a heat of nitride formation of at least 4.50. Any composition below the line 22-24 or its extension 2l has a heat of oxideformation of at least 7.10. Accordingly the area 22-23-24 represents compositions having both a heat of oxide formation y of at least 7.10 and a heat of nitride formation of at least 4.50. It will be noted from this diagram also that the inclusion of silicon in the composition rapidly decreases the ranges of titanium and zirconium which can be used and still give satisfactory heat values. When the silicon exceeds about 25%, no combination of titanium and zirconium will give the heat values` of 7.10 and 4.50.

It is preferred that the percentages of titanium, zirconium and silicon in their active form when calculated on the basis that said active elements in active form constitute 100%, fall within the area 50-5I-24 in the ternary diagram of Fig. 3. Alloys containing titanium, zirconium and silicon are advantageous as compared to similar alloys not containing titanium in that their reaction products are such that the properties of the steel to which the alloy is added are improved and the.physical and chemical properties of the alloy such as specific gravity, solubility in steel, and melting point are improved. It is preferred that the percentages of the elements as above referred to fall within the more restricted area 50-52-151 The ternary diagram for the system zirconiumaluminum-silicon is shown in Fig. 4. All compositions below the line 28--29 have a heat of oxide formation of at least 7.10. All compositions to the' left of the line 30-3I have a heat of ynitride formation of at least 4.50. Accordingly, all compositions within the area 32--3I-33-28 have a heat of oxide formation of at least '7.10 and a heat of nitride formation of at least 4.50.

In determining Whether an alloy which s to be added to iron or steel falls within any of the areas shown on any of the Figures 1 through 4, it should be borne in mind'that these ternary diagrams have been constructed on the basis of the active elements in their active form constituting 100%. Therefore, in figuring whether or not a given alloy comes within the defined lareas the following method is to be used:

1. Only the active elements in the alloy, as previously described, are to be considered.

2. The subversive elements as previously referred to, such, for example, as silicon and carbon, are to be considered and one must calculate the amount of 'active elements which combine with the subversive elements and from this it is determined how much of each active element in active form exists in the alloy.

3. The active elements in active form are to be considered as constituting 100%.

4. If the percentages of active elements in their active form fall within the areas referred to, they are adequate so far as the heat of oxide formation and the heat of nitride formation are concerned.

The ternary systems shown in Figs. 1, 2 and 4 include aluminum as one of the elements. The elements magnesium, calcium, barium and strontium influence the composition in a manner quite similar to aluminum, since their heats of oxide formation and heats of nitride formation are generally of thevsame order. Accordingly the areas defining the compositions as referred to when the composition contains aluminum are also generally true when the composition contains one or more of the elements magnesium, calcium, barium or strontium. The exact values when the composition contains any of these elements magnesium, calcium, barium or strontium can be readily calculated.

In Fig. 1, I have shown the ternary diagram titanium-zirconium-aluminum yand in Figs. 2, 3 and 4 I have shown ternary diagrams of silicon with each of the possible combinations of any two of titanium, zirconium and aluminum. From these four ternary diagrams, a solid can be readily constructed which will represent the quaternary system titanium, zirconium, aluminum and silicon and all compositions coming within that solid will have a heat of oxide formation of at least-7.10 and a heat of nitride formation of at least 4.50.

As has been pointed out previously, iron or steel baths always contain more or less nitrogen and oxygen and it is an object of the present invention to x or remove these constituents. As an example, steel of the type known as SAE 4615, which is a low carbon nickel molybdenum steel,

. may contain from .001 to .100% oxygen, when 1. Preparation of a suitable steel bath.

2. Addition to the bath of a nitrogen deactivator or a nitrogen deactivator and a deoxidizer.

3. Prevention or suppression of renitrication of the steel.

1. In the preparation of a suitable steel bath, the usual or. any desired steps of melting, refining and adjusting of composition may be employed. The refining may involve the use of slags and ores for reducing the sulphur and phosphorus to the desired amountI and otherwise adjusting the composition of the steel. It may include the addition of ferro-alloys. The effect of the melting andrefining operations is to produce a steel bath having approximately the content of carbon, silicon, manganese, sulphur and phosphorus which is desired in the nal steel. 'I'he steel does,

' however, contain nitrogen and oxygen, which it is desired to deactivate by the use of reaction alloys. v

After a suitable steel ba-th has been prepared by melting and refining, it is generally advisable to add a deoxidizer such as aluminum but, if desired, the deoxidizer may be omitted, provided that the alloy subsequently added for fixing the nitrogen also contains a-deoxidizer.

2. The next step is the addition to the steel y bath of a nitrogen deactivator which may, for example, be titanium or zirconium or an alloy or intimate mixture of both titanium and zirconium. In place of the alloy or mixture, I may use titanium and zirconium added either simultaneously or subsequently. It is preferred, however, that the titanium and zirconium or other nitrogen deactivator be 'used in the form of lan alloy rather than as separate or simultaneous additions of mere mechanical mixtures of the deactivators. In selecting an alloy or mixture of active elements, it is preferred that they contain preventing or inhibiting renitriflcation of the steel. One way of accomplishing this is toadd the alloy in amount suicient so that the steel when solidified contains a residual of active eleboth a nitrogen deactivator such as titanium or v zirconium, which has a strong aillnity for nitrogen, and a deoxidizer, such as aluminum or magnesium or other strong deoxidizer which has a stronger afiinity for oxygen than does the nitro- Agen deactivator. By the use of a combination of stable insoluble nitrides with the nitrogen in thev steel under the conditions that prevail'in a steel bath. Although a nitrogen deactivator itself, for example titanium or zirconium, would be suitable by themselves to form insoluble nitrides if the steel did not have access to oxygen, under the conditions which prevail generally in'steel makments from the alloy. That is, the alloy is added in an .amount which is in excess of that required to deoxidize and denitrogenize the steel and sufficient to prevent renitriiication and reoxidation. It will'be seen that if the alloy is added at an early stage of the process more alloy may be required than if added at a later stage, in order to insure that in both cases there will be some residual of active elements in the steel when it solidies. Y

From 'the point of view of preventing l'ss of the alloy itself and insuring a, residual of the active elements in the steel, it is preferred to add the alloy to the steel in the ingot mold. The mold itself acts as a protection against renitriflcation and reoxidation and in addition the time during which these phenomena could occur is at a minimum. For practical reasons, however, it may be desired to add the alloy either in the ladle or in some cases inthe furnace or in other cases during pouring from the furnace to -the -ladle or from the ladle to the ingot mold. Generally no special precautions need be taken when the alloy is added to the steel in the ladle, unless it is to be held there an undue length of time, because ordinarily there is sufficient slag formed on the top of the ladle to protect the steel against reoxidation and renitrication. However,I it has been observed that a slightly larger amount of alloy is required where the alloy is added to the ladle over that required where it is added to the ingot mold. Where the alloy is added to the steel in the furnace, even larger amounts of the reaction alloy are required as the opportunity for reoxidation and renitrincation is increased. Re-

ing, the steel has access to both oxygen and nitro- I an average heat of oxide formation according to y Equation V of at least 7 and an average heat of nitride formation according to Equation VI of at least 4.25. The alloy should, of course, in addition, have the other properties, such as suitable specilc gravity, solubility, etc. previously'referred to. I have found that in using an alloy containing about 20% titanium, 20% aluminum and 7% zirconlum'as active elements and having a heat of oxide formation over '1 and a heat of nitride formation of over 4.25 an amount of alloy of about 2te 6 p'ounds 'per ton is sulcient to effectively deactivate nitrogen and 4oxygen in treating basicopen hearth steel. ,l

The amount of alloy needed -for any given condition is, of course, a function of both the heat of oxide formation and nitrogen formation and the oxygen and nitrogen equivalent-of the alloy.

oxidation and renitrication can be suppressed or prevented by some mechanical means, such as the use of a protective slag, a. protective covering of coke or by carrying out the operation in aclosed container.

The amount of reaction alloy added to the steel will vary according to the nitrogen and oxygen content of the steel and according to the degree of denitriiication and deoxidation which is desired and upon the time and the conditions under which the reactionv alloy is added. There are two general ways in which the amount of reaction alloy to beadded may Ibe determined. I may add an 'amount of the alloy which from past experience I know is sumcient to provide an excessof the active elements in the steel when it has solidified. Thus I may add say four Ipounds of the alloy per. ton to each heat of basic 'open hearth steel that is made. If it is found that in some instances this produces a residual of active elements in the steel and in other cases it does not, then, of course, the amount of reaction alloy should be increased. In this manner, I arrive at an amount of alloy per ton which should be added to'each heat and which will insure that there will always be an excess of. active ingredients in the steel when it has solidified under the conditions of manufacture which prevail for that steel. This method is simple in that no tests are thereafter required for each lindividual heat to determine what amount of reaction alloy shall be used but it is objectionable in that the amount of alloy added vis morein ysome cases than is actually required to produce the desired results-that is,

desired degree of -de'nitriflcation and deoxidation'.L

It will be understood that the contents of nitrogen and oxygen vary from heat to heat and, therefore,

in order to insure that there will always be an excess of the active elements in the steel when solidified, it is necessary in practice to use an amount which under some circumstances would be more than sucient to produce the desired result.

The other and more eilicient method of determining the amount of reaction alloy is to test the steel to determine some properties which are affected by the nitrogen content of the steel and are altered by the alloy addition. I have found that these properties which I measure are dependent upon the 'active nitrogen content of the st eel and, therefore, the test which I make is an indication of the relative active nitrogen content of the steel as compared with a known standard. In this way, a rapid determination of the amount of alloy which should be added may be made and then the alloy is added in accordance with the determination, in order to produce whatever degree of denitrication may be desired. Thus I use only approximately the amount of reaction alloy which is required to produce the desired effects in each individual heat.

The preferred method of testing for the nitrogen content of a steel bath is as follows. A sample of the steel is taken from the bath after the bath has reached the point where it is ready for alloy addition and the sample is cast into a block having a length of 4 and a width and thickness of about 11/2". This is to be compared with astandard sample of the same dimensions and of the same chemical composition as far as carbon, manganese, silicon, phosphorus and sulphur and alloying elements are concerned, but which contains a low nitrogen content. 'I'he actual size of the standard and sample may be different from that described lbut each should bev of substantially the same dimensions as the other. The sample block and the standard block are placed in Aa furnace and a pyrometer is connected to each block in such manner that the difference in temperature between the sample and the standard may be recorded. The standard and sample are locatedin the furnace so as to be under as nearly identical furnace temperature conditions as possible and the entire setup so arranged that -any difference in temperature between the standard and sample is due to differences in evolution or absorption of heat from reactions within the two steels themselves during heating or cooling. I may use resistance pyrometers, optical pyrometers, thermocouples or any other type of temperature measuring instruments which can be arranged and are of sullicient sensitivity to measure differences in 'temperature between the sample and the standard. Referring to Fig. 5, which illustrates in a diagrammatic way one suitable arrangement, the standard block 60 and the sample block 6| are placed in a furnace 62 and are connected to a recording instrument 63, as indicated; The hot junction 84 is placed in the standard and the cold junction 65 is placed in the sample, or vice versa, and connected by the wire 66, and the other wires 61 and 68 are connected to the indicating instrument 63. The indicator thus shows the difference in temperature between the standard and the sample. In order to record at what actual temperatures. there are differences in temperatures lbetween the standard and the sample, a

The temperature of the furnace 'is raised to some selected temperature above the critical points of the standard and sample (which are the same), say l600 F., and the standard and sample are allowed to cool. The cooling' rate is not critical. It may be either fast or slow. I have found that a cooling rate of even 25 F. per minute through the critical range is satisfactory but this rate is slower than would be convenient for routine testing. The cooling rate preferably is of the same order as that which occurs when the article made from the steel in question is quenched in order to harden it. The differences in temperature between the standard and the vsample when they are passing through their critical ranges are noted and these differences in temperatures are used to determine the amount of alloy, if any, which need be added to the steel.

Fig. 6 represents in a diagrammatic manner the curves which may be obtained in carrying out the test as above referred to. The vertical ordinate represents temperatures in degrees F. and the horizontal'ordinate represents the difference in temperature between the standard and the sample for any given temperature. When the furnace has been heated to a selected temperature, say l600 F., the standard and sample are both at the same temperature and they remain at substantially the same temperature as they are cooled down to a certain point. The composition of the standard block and of the sample block, the curves of which are represented in Fig. 6, was that of a T1340 steel containing.

Per cent Carbon .43 Manganese 1.77 Silicon 0.24 Phosphorus 0.25 Sulphur 0.28

with the following exception. The standard had been treated to deactivate nitrogen, so that it contained only between .001 and .002 active nitrogen and about .005 total nitrogen, whereas the sample was the same steel, except that it had not been treated to deactivate nitrogen and second thermocouple 69 is placed in the furnace,

contained a total of .007 nitrogen and an active nitrogen of .005. Considering this particular sample, and standard, it will be noted that at l300 F. there is no difference in temperature between them and that there is no difference in temperature down to about 1260 F. At this point, the steels enter their critical range and the curve B bears to the left from the normal curve A and the curve B remains displaced from the normal curve down to a temperature of about 1200 F. The fact that curve B departs from the normal curve A shows that during this critical range there is a difference in temperature between the sample and the standard. This difference in temperature between the standard and the sample is linked up with the rate of transformation of the standard and sample through their critical ranges, such as the transformation from austenite' to martenslte, from martensite to troostite, from troostite to sorbite and pearlite. This deviation is dependent both upon the differences of rates of the above changes as well as the amount of heat evolved during the reaction. This deviation of the curve B from the normal curve A shows that the active nitrogen in the sample is greater than the active nitrogen in the standard and, therefore, the hardenability of the sample is not as great as the hardenability of the standard. I wish to decrease the nitrogen in the steel bath and I, therefore, add an alloy which may be. say, 20% titanium, 20% aluminum and 7.5% zirconium, with the balance iron. Assume that I add one pound of this alloy per ton and obtain another sample and test the second sample against a standard in the same way as has been described. It Will be found that the curve C, which represents the difference in temperature between the standard and the sample, is moved to the right, that is toward the normal curve A. If increasing amounts of the alloy are added to the steel bath and other samples are taken and other tests are made, it will be found that the normal curve A is reached showing that the steels are behaving alike. In fact, by the addition of suilicient alloy it is possible to produce a curve D which lies on the opposite side of the normal from the curve B, provided that the normal curve A represents an amount of nitrogen which is not the lowest amount which can be obtained by adding alloy to the steel.

I have described a preferred method of testing for the effects of nitrogen in a steel or more broadly a method of testing to determine a behavior of a steel which is related to its active nitrogen content. It is to be understood, however, that vthe invention is not limited to the preferred testing method. Other methods may be employed, even though not as desirable', and after the test has been performed alloy lmay be HIN added to bring the steel to some desired degree of uniformity. I believe that the desired properties in steel, for example hardenability and other physical properties such as tensile strength, impact values, magnetic properties and dynamic properties, are dependent upon the state and content of nitrogen and oxygen in the steel. I have found that this test gives me valuable information in determining how much, if anyalloy should be added to bring the steel within a given degree of uniformity of physical characteristics.

Reaction alloys according to the present invention may lbe made by the electric furnace process, the aluminothermic process or by a combination of such processes.

Although I have described certain preferred embodiments and procedures for carrying out the invention, it is to be understood that the invention is not so limited but may be other- Wise embodied or practiced within the scope of the following claims.

I claim:

1. The process of making steel, which comprises obtaining a sample of steel from a bath of steel, obtaining a standard the physical properties of which are known and has substantially the same chemical composition as the sample except for active nitrogen, testing the sample and standard by means which indicate the relative contents of active nitrogen in the sample and standard, and adding to the bath of steel nitrogen deactifying material in accordance with the test to produce steel having the desired physical properties.

2. An alloy for addtion`to iron or steel, conearth metals and alkali-metals being sufficient to combine with the silicon and leave not over about 10% of silicon in active form, an effective amount up to about 40% of at least one of the elements of the group consisting of tantalum, uranium, molybdenum, tungsten and manganese, the balance being one or more elements which are not subversive of the reaction characteristics of the alloy, the alloy having an average heat of oxide formation per gram of oxygen according to the formula @pillo-(Mei)HCILhHO-(Mer1)+knrh1n-(MGIHH CI(M1)HCH-(M611)+kI1I-(Me1r1)+ of at least 7.0 and a heat of nitride formation per gram of nitrogen according to the formula of at least 4.25 said alloy having an oxygen equivalent of at least 10 grams of oxygen per 100 grams of alloy according to the formula and a nitrogen equivalent of at least 5 grams of nitrogen per 100 grams of alloy according to the formula Ni0o=l1.(Me1) +111.(Me11) +1111. (M6111) not over about 10% of silicon in active form, the

titanium and'zirconium or either of them being present in amount suiiicient to react with the carbon and leave at least about 10% of titanium or zirconium or both of them in active form, an

eiective amount up to 40% of at least one ele-v ment of the group consisting of tantalum, uramum, molybdenum, tungsten and manganese, the balance being one or more elements which are -,not subversive of the reaction characteristics of the alloy, the Valloy having an average heat of oxide formation per gram of oxygen according to the formula of at least 7.0 and a heat of nitride formation per grain of nitrogen according to the formula H WON of at least 4.25 said alloy having an oxygen equivalent of at least 10 grams of oxygen per 100 grams of alloy according to the formula O1 ou :161. (Mer) -I-kni (Men) +7C111.(M em) and a nitrogen equivalent of at least 5 grams vof 

